NiCo2S4/MoS2 Nanocomposites for Long-Life High-Performance Hybrid Supercapacitors

Metal sulfides (MS) and mixed metal sulfides (MTMS) have been considered potential candidates over their metal oxide/mixed metal oxide counterparts in recent years. Herein, one MTMS, i.e., NiCo2S4, was combined with 2D MS MoS2 through a single-step solvothermal process with different morphologies (sheet-like and rod-like) for supercapacitor applications. The resulting electrode exhibited excellent coulombic efficiency, high specific capacitance, superior energy density, and, most importantly, ultra-high cycling stability. In particular, the electrode delivered a capacitance of 2594 F g−1 at 0.8 A g−1 after 45,000 charge/discharge cycles with a remarkable stability of 192%. Moreover, the corresponding hybrid supercapacitor device displayed an impressive coulombic efficiency of 123% after 20,000 cycles and 118% after 45,000 cycles. In addition, the device also exhibited a decent energy density of 31.9 Wh kg−1 and good cycling stability of 102% over 15,000 cycles.


Introduction
Fossil fuel resources are predicted to be depleted in the next few decades. Therefore, developing renewable and clean energy conversion/storage systems will play a key role in fulfilling the future energy demand. Researchers have been exploring innovative synthetic approaches to fabricate advanced energy storage devices for the last few decades. However, it is challenging to explore easy and inexpensive synthesis methods which are industrially viable. Apart from this, economic efficiency is also one of the most critical factors for long-term operation. In this aspect, supercapacitors are considered favorable, clean electrochemical energy storage devices because of their high power density (P D ), high cycle life, and fast charge/discharge ability [1][2][3][4][5].
Supercapacitors can be ordinarily classified into three groups on the basis of their electrochemical storage kinetics: electrical double-layer capacitor (EDLC), pseudocapacitor, and hybrid capacitor (a combination of EDLC and pseudocapacitor). Typically, pseudocapacitor electrodes are fabricated from transition metal oxides and conducting polymers. On the other hand, EDLCs mostly use carbonaceous materials. In general, EDLC exhibits comparatively lower specific capacitance (C sp ) and energy density (E D ) than pseudocapacitors because of the fast, reversible redox reactions at the electrode-electrolyte interface of electrodes. However, EDLC has good intrinsic conductivity, chemical stability, P D , and cycle life. Overall, hybrid capacitors are the best choice for next-generation electronic devices, combining the advantages of both EDLC and pseudocapacitors to produce advanced high-performance supercapacitors [6].
Nevertheless, the E D of commercialized supercapacitors is still lower than that of batteries and fuel cells, despite being higher than that of conventional dielectric capacitors [7,8]. The E D can be enhanced by altering several strategies such as improving the voltage window of the electrolyte, combining the carbon materials with metal oxide/mixed metal oxides, or integrating different pseudocapacitive/battery-type electrodes [9]. Among the transition metals, Ni and Co are rich in valence electrons. Therefore, such metals considerably impact supercapacitors with their rich electrochemical activity. Moreover, their corresponding MTMS, such as NiCo 2 S 4 , exhibit superior faradaic behavior to those of mono-metallic sulfides counterparts, such as NiS and CoS [10][11][12], and higher electrical conductivity than bimetallic NiCo 2 O 4 [13]. In addition, the 2D layered compound of Mo, such as MoS 2 , has both the metallic 1T phase and the semiconducting 2H phase [14,15]. Such 2D material also has a small bandgap of 1.2~1.9 eV that can be used in nanoelectronics [16]. It is important to note that the characteristics of MoS 2 are similar to another carbonaceous 2D material, i.e., graphene. However, MoS 2 has better capacitive characteristics than graphene. It also displays faster intrinsic ionic conductivity than oxides [17,18].
In the present work, NiCo 2 S 4 is combined with MoS 2 to develop a hybrid supercapacitor device. Herein, MoS 2 is chosen as one of the components as the bulk MoS 2 is composed of metallic Mo-layers sandwiched between two sulfur layers held together by weak van der Waals interactions. Hence, the electrolyte ions can diffuse quickly and intensely into the material and increase the electrochemical charge storage properties. Interestingly, NiCo 2 S 4 only uses the anions of the electrolyte in the charging process, whereas MoS 2 uses the cations of the electrolyte during the discharge process. Later, such charge−discharge characteristics tend to enhance the overall electrochemical properties of the supercapacitors. Benefiting from the MS and MTMS, the electrode exhibited excellent C sp after 45,000 charge/discharge cycles. Moreover, the corresponding hybrid device demonstrated good cycling stability over 15,000 cycles and decent E D .

Synthesis of NiCo 2 S 4 -MoS 2 Composites
The NiCo 2 S 4 -MoS 2 composite was synthesized by the one-step solvothermal approach. The precursors, 0.3 g Ni(NO 3 ) 2 , 0.6 g Co(NO 3 ) 2 , 2 mL C 2 H 8 N 2 (ethylenediamine), 0.8 g C 2 H 5 NS (thioacetamide), and different amounts (0.05 and 0.15 g) of Na 2 MoO 4 were dissolved and mixed in 30 mL C 2 H 6 O 2 (ethylene glycol) with constant stirring and shifted to a Teflon-lined autoclave. The solution-filled autoclave was heated at 200 • C for 15 h and then cooled down. After the completion of the reaction, the material was filtered, washed, and dried at 60 • C for 12 h. Two composites with dissimilar morphologies called NCMS-L (NiCo 2 S 4 /MoS 2 with low Mo content) (sheet-like) and NCMS-H (NiCo 2 S 4 /MoS 2 high with Mo content) (rod-like) were produced using low (0.05 g) and high (0.15 g) amounts of Na 2 MoO 4 , respectively.
Furthermore, bare NiCo 2 S 4 and bare MoS 2 were also synthesized using the abovementioned procedures in the absence of Mo 6+ for bare NiCo 2 S 4 and Ni 2+ and Co 2+ for bare MoS 2 , respectively.

Synthesis Mechanism of NiCo 2 S 4 /MoS 2 Composite
The current work is focused on developing two different morphologies of the composite of NiCo 2 S 4 and MoS 2 . A schematic diagram demonstrates the formation mechanism of these two morphologies ( Figure 1). Initially, Ni(NO 3 ) 2 , Co(NO 3 ) 2 , and Na 2 MoO 4 were dissolved in ethylene glycol to form Ni 2+ , Co 2+ , and MoO 4 2− ions. It is important to note that the rapid transportation of MoO 4 2− was restricted by its high molar mass and the high viscosity of ethylene glycol solvent. Additionally, the formation of stable NiCo 2 S 4 took longer time than MoS 2 . Therefore, MoO 4 2− was first combined with H 2 S to form amorphous MoS 2 . Therefore, no apparent peaks of MoS 2 are observed in the XRD patterns of the composite materials (Figure 2a−c). With the assistance of the -NH 2 group in thioacetamide, Ni 2+ and Co 2+ formed stable complexes on the surface of MoS 2 and then reacted with H 2 S to produce NiCo 2 S 4 [19]. On the other hand, the morphology of composite material changed from sheet-like to rod-like by increasing the concentration MoS2. Therefore, no apparent peaks of MoS2 are observed in the XRD patterns of the composite materials (Figure 2a−c). With the assistance of the -NH2 group in thioacetamide, Ni 2+ and Co 2+ formed stable complexes on the surface of MoS2 and then reacted with H2S to produce NiCo2S4 [19]. On the other hand, the morphology of composite material changed from sheet-like to rod-like by increasing the concentration of the precursor Na2MoO4.2H2O from 0.05 g to 0.15 g (Figure 3a−d). Probable reactions during the solvothermal process are shown below: CH3CSNH2 + H2O → CH3CONH2 + H2S (1) Ni 2+ + 2Co 2+ + 4H2S → NiCo2S4 + 4H2 (3)   longer time than MoS2. Therefore, MoO4 was first combined with H2S to form amorphous MoS2. Therefore, no apparent peaks of MoS2 are observed in the XRD patterns of the composite materials (Figure 2a−c). With the assistance of the -NH2 group in thioacetamide, Ni 2+ and Co 2+ formed stable complexes on the surface of MoS2 and then reacted with H2S to produce NiCo2S4 [19]. On the other hand, the morphology of composite material changed from sheet-like to rod-like by increasing the concentration of the precursor Na2MoO4.2H2O from 0.05 g to 0.15 g (Figure 3a−d). Probable reactions during the solvothermal process are shown below: CH3CSNH2 + H2O → CH3CONH2 + H2S (1) Ni 2+ + 2Co 2+ + 4H2S → NiCo2S4 + 4H2 (3)   The change in morphology with altering the concentration of MoO 4 2− can be attributed to the change in the direction of diffusion of MoO 4 2− during its ion-exchange process with S 2− . The inward diffusion of MoO 4 2− produced sheet-like morphology, whereas the outward diffusion resulted in the synthesis of a rod-like composite [20]. The change in morphology with altering the concentration of MoO4 2− can b tributed to the change in the direction of diffusion of MoO4 2− during its ion-exchange cess with S 2− . The inward diffusion of MoO4 2− produced sheet-like morphology, wh the outward diffusion resulted in the synthesis of a rod-like composite [20].

Characterization and Morphology of NiCo2S4/MoS2 Composite
The crystallinity of composite materials was examined by XRD analysis ( Figure S1). Moreover, the concentration of precursor Mo 6+ was compared to Ni 2+ and Co 2+ , which generates dominant peaks of NiCo2S4 to suppres peaks of MoS2. The XRD pattern of bare amorphous MoS2 confirms the amorphous n ( Figure 2a). In addition, the absence of any secondary peak in the XRD pattern o composites indicates their high purity. A similar XRD pattern has also been observe NCMS-H ( Figure 2c). The morphologies of bare NiCo2S4 and MoS2 and their compo were analyzed by FESEM, as shown in Figure 3a−d. Both bare NiCo2S4 and MoS2 di the presence of aggregated clusters. However, compared with MoS2, NiCo2S4 s bigger clusters. On the other hand, composite materials NCMS-L and NCMS-H ex sheet-like and rod-like morphology, respectively. From the morphological analysis confirmed that NCMS-L displays higher porosity than NCMS-H. This fact also exp why the capacitance retention of NCMS-L was better than NCMS-H after cycling (Figures 7d and S6d) [13,21,22]. Furthermore, TEM analysis was performed to exa the microstructure of the electrode materials. As shown in Figure 4a, NCMS-L displ porous sheet-like structure. On the contrary, NCMS-H shows a rod-like structure (F 4b). Therefore, it is essential to note that the SEM images support the TEM analysis r On the other hand, Figure 4c,d shows the structure of MoS2 and NiCo2S4, respecti

Characterization and Morphology of NiCo 2 S 4 /MoS 2 Composite
The crystallinity of composite materials was examined by XRD analysis (Figure 2a Figure S1). Moreover, the concentration of precursor Mo 6+ was low compared to Ni 2+ and Co 2+ , which generates dominant peaks of NiCo 2 S 4 to suppress the peaks of MoS 2 . The XRD pattern of bare amorphous MoS 2 confirms the amorphous nature ( Figure 2a). In addition, the absence of any secondary peak in the XRD pattern of the composites indicates their high purity. A similar XRD pattern has also been observed for NCMS-H (Figure 2c). The morphologies of bare NiCo 2 S 4 and MoS 2 and their composites were analyzed by FESEM, as shown in Figure 3a−d. Both bare NiCo 2 S 4 and MoS 2 display the presence of aggregated clusters. However, compared with MoS 2 , NiCo 2 S 4 shows bigger clusters. On the other hand, composite materials NCMS-L and NCMS-H exhibit sheethology, respectively. From the morphological analysis, it is confirmed that NCMS-L displays higher porosity than NCMS-H. This fact also explains why the capacitance retention of NCMS-L was better than NCMS-H after cycling tests (Figures 7d and S6d) [13,21,22]. Furthermore, TEM analysis was performed to examine the microstructure of the electrode materials. As shown in Figure 4a, NCMS-L displays a porous sheet-like structure. On the contrary, NCMS-H shows a rod-like structure (Figure 4b). Therefore, it is essential to note that the SEM images support the TEM analysis result. On the other hand, Figure 4c,d shows the structure of MoS 2 and NiCo 2 S 4 , respectively. However, the NiCo 2 S 4 particles are found to be larger and denser than MoS 2 . Owing to the small-sized particles and amorphous structure of MoS 2 , the electrolyte can pass easily inside the composite material and enhance the redox reaction to deliver high C sp .   (Figure 5a). The deconvoluted Ni 2p core-level spectrum shows four peaks. Herein, two spin-orbit doublets correspond to Ni 2+ and Ni 3+ [23]. Furthermore, two shake-up satellites (identified as "Sat.") have also been observed (Figure 5b). On the other hand, two spin-orbit doublets in Co 2p spectrum can be designated as Co 2+ and Co 3+ [24]. Moreover, one shake-up satellite has also been observed (Figure 5c). The S 2p spectrum is deconvoluted into two significant peaks and a shake-up satellite peak with binding energies of 162.8 and 161.6 eV, corresponding to S 2p1/2 and S 2p3/2, respectively, as shown in Figure 5e [25].  (Figure 5a). The deconvoluted Ni 2p core-level spectrum shows four peaks. Herein, two spin-orbit doublets correspond to Ni 2+ and Ni 3+ [23]. Furthermore, two shake-up satellites (identified as "Sat.") have also been observed (Figure 5b). On the other hand, two spin-orbit doublets in Co 2p spectrum can be designated as Co 2+ and Co 3+ [24]. Moreover, one shake-up satellite has also been observed (Figure 5c). The S 2p spectrum is deconvoluted into two significant peaks and a shake-up satellite peak with binding energies of 162.8 and 161.6 eV, corresponding to S 2p 1/2 and S 2p 3/2 , respectively, as shown in Figure 5e [25].
The Mo 3d XP spectrum in Figure 5d shows two strong peaks at 228.8 and 232.4 eV, which can be assigned to the Mo 3d 5/2 and Mo 3d 3/2 doublet, respectively. The peak at 226.2 eV is assigned to S 2s [20]. Furthermore, to determine the presence of Mo in the composite material, EDX elemental mapping was performed for NCMS-L through HR-TEM analysis (Figures 6 and S2). As expected, the concentration of Mo is lower than the other elements, Ni, Co, and S. However, all elements are distributed uniformly. From EDX analysis, it can be concluded that MoS 2 can cooperate and enhance the electrochemical properties of NiCo 2 S 4 to obtain promising electrochemical performance.

Electrochemical Properties of NiCo 2 S 4 /MoS 2 Nanocomposite
The CV (cyclic voltammetry), GCD (galvanostatic charge/discharge), and EIS (electrochemical Impedance Spectroscopy) tests were performed to explore the electrochemical properties of NCMS-L, NCMS-H, bare MoS 2 , and bare NiCo 2 S 4 electrodes in a 3 M KOH electrolyte. Figure 7a represents the CV curves of NCMS-L within the potential limit of 0 to 0.6 V at various scan rates of 5-100 mV s -1 . The CV curves reveal faradaic behavior, in which a pair of prominent redox peaks are observed. Similarly, NiCo 2 S 4 and MoS 2 electrodes also have a pair of redox peaks at different scan rates (Figures S4 and S5). The corresponding redox reactions can be expressed as follows [14,15,21,[26][27][28][29][30]: CoSOH NiS Nanomaterials 2023, 13, x FOR PEER REVIEW The Mo 3d XP spectrum in Figure 5d shows two strong peaks at 228.8 and 2 which can be assigned to the Mo 3d5/2 and Mo 3d3/2 doublet, respectively. The peak eV is assigned to S 2s [20]. Furthermore, to determine the presence of Mo in the com material, EDX elemental mapping was performed for NCMS-L through HR-TEM a (Figures 6 and S2). As expected, the concentration of Mo is lower than the other el Ni, Co, and S. However, all elements are distributed uniformly. From EDX analysi be concluded that MoS2 can cooperate and enhance the electrochemical prope NiCo2S4 to obtain promising electrochemical performance. The GCD test of NCMS-L, bare NiCo 2 S 4 , and bare MoS 2 are performed at the constant currents of 1, 3, 5, 8, and 10 mA (or corresponding current densities of 0.8, 2.3, 3.8, 6.2, and 7.7 A g −1 ). Based on the GCD and CV curves, the C sp of the electrodes was calculated using the following equations: where I is the response constant current (A); t is the discharge time (s); ∆V is the potential window of the CV or GCD curves (V); m is the mass of active material (g); i and V are current and potential in the CV curve (A and V), respectively, and ν is the scan rate (V s -1 ) [31].

Electrochemical Properties of NiCo2S4/MoS2 Nanocomposite
The CV (cyclic voltammetry), GCD (galvanostatic charge/discharge), and EIS (electrochemical Impedance Spectroscopy) tests were performed to explore the electrochemical properties of NCMS-L, NCMS-H, bare MoS2, and bare NiCo2S4 electrodes in a 3 M KOH electrolyte. Figure 7a represents the CV curves of NCMS-L within the potential limit of 0 to 0.6 V at various scan rates of 5-100 mV s -1 . The CV curves reveal faradaic behavior, in which a pair of prominent redox peaks are observed. Similarly, NiCo2S4 and MoS2 electrodes also have a pair of redox peaks at different scan rates (Figures S4 and S5). The corresponding redox reactions can be expressed as follows [14,15,21,[26][27][28][29][30]: CoSOH + OH − ↔ CoSO + H2O + e − NiS + OH − ↔ NiSOH + e − MoS2 + K + + e − ↔ MoS-SK MoS2 + K + + e − ↔ MoS2-K (8) The C sp of NCMS-L was calculated to 1390, 1000, 864, 756, and 698 F g −1 at the currents of 1, 3, 5, 8, and 10 mA (corresponding current densities of 0.8, 2.3, 3.8, 6.2, and 7.7 A g −1 ), respectively (Figure 7b). It is important to note that the GCD profiles indicate significant deviation from the ideal rectangular shapes, indicating the Faradaic characteristics. The cycling stability of the electrode was assessed by continuing the CV test for 45,000 cycles at the scan rate of 100 mV s −1 , as presented in Figure 7c,d. The electrode exhibited superior capacitance retention of 135% over the first 8000 cycles. However, after these initial cycles, the capacitance retention gradually increased to 149% for up to 35,000 cycles, which is associated with the activation of the electrode material. For further activation of the electrode and to check the electrode's feasibility for long-term stability, the cycling process was stopped for one week with the electrode soaked in the electrolyte solution. The cycling test continued up to the 45,000th cycle. We found that soaking the electrodes in the electrolyte for a long time (after activation) was quite favorable for enhanced cycling stability. Such drastic enhancement in electrochemical performance is associated with the Nanomaterials 2023, 13, 689 8 of 14 electrochemical reconstruction of the electrode materials during cycling and soaking the electrode in electrolyte solution for a long time [32]. It is important to note that, after the soaking process, the capacitance retention increased to 207% at the 38,000th cycle, which can be associated with the re-activation of the electrode. However, the capacitance then gradually decreased and reached 192% of its initial capacitance at the 45,000th cycle due to the structural breakdown, as depicted in Figure S3. The GCD test of NCMS-L, bare NiCo2S4, and bare MoS2 are performed at the constant currents of 1, 3, 5, 8, and 10 mA (or corresponding current densities of 0.8, 2.3, 3.8, 6.2, and 7.7 A g −1 ). Based on the GCD and CV curves, the Csp of the electrodes was calculated using the following equations: where I is the response constant current (A); t is the discharge time (s); ΔV is the potential window of the CV or GCD curves (V); m is the mass of active material (g); i and V are current and potential in the CV curve (A and V), respectively, and ν is the scan rate (V s -1 ) [31].
The Csp of NCMS-L was calculated to 1390, 1000, 864, 756, and 698 F g −1 at the currents The cycling stability increased to 207% at the 38,000th cycle; after that, it decreased slightly to 192% at the 45,000th cycle. The GCD test examined the retention of the specific capacitance of NCMS-L at 1 mA (Figure 7e). The C sp was enhanced from 1390 to 2293 F g −1 at the 20,000th cycle and 2594 F g −1 at the 45,000th cycle. Moreover, the coulombic efficiency increased from 73% to 123% at the 20,000th cycle and then slightly decreased to 118% at the 45,000th cycle. Figure 4f shows the corresponding Nyquist plots at the 1st, 35,000th, and 45,000th cycles. The intercept at the y-axis in the high-frequency region that signifies the equivalent series resistance (ESR) was 0.45 Ω (1st cycle), 0.49 Ω (35,000th cycle), and 0.39 Ω (45,000th cycle), respectively. The increase and decrease in ESR over the cycles are Nanomaterials 2023, 13, 689 9 of 14 agreed well with the change in capacitance over the long-term cycling stability. Similar trends have also been found for NiCo 2 S 4 and MoS 2 , as shown in Figures S4c and S5c.
Comparing CV curves of MoS 2 , NiCo 2 S 4 , and NCMS-L at a scan rate of 100 mV s −1 displays the highest current response for the composite (Figure 8a). The comparative GCD plots at the current of 1 mA also designate a higher discharge time of NCMS-L than its monometallic and bimetallic counterparts (Figure 8b). Figure 8c represents the CV curves of NiCo 2 S 4 at different cycles at the constant scan rate of 100 mV s −1 . Compared to the 1st cycle, a significant change in CV pattern is observed at the 5000th cycle. This fact indicates the gradual activation of the electrode material. However, the CV curves' redox characteristics do not alter after 1000 cycles, indicating good electrochemical stability. Most importantly, the electrode displayed a good cycling stability of 147% after 5000 cycles (Figure 8d). A similar pattern has also been observed for the MoS 2 electrode (Figure 8e). Nevertheless, the MoS 2 displayed better cycling stability (248%) than NiCo 2 S 4 over 5000 cycles (Figure 8f). Similar to other supercapacitor electrodes, the area under the CV profiles increases with increasing the scan rate for NiCo 2 S 4 ( Figure S4a). The faradaic charge storage characteristics are visible from the GCD profiles at different current densities ( Figure S4b). It is important to note that the discharge time was increased after 5000 cycles ( Figure S4d). Likewise, the capacitance of NiCo2S4 was increased from 947 to 1121 F g −1 after 5000 cycles. Figure S5a−d represents the electrochemical data for MoS2. Similar to NiCo2S4, the faradaic charge storage ability of MoS2 is visible from their CV curves and GCD profiles ( Figure S5a,b. However, the cycling stability of MoS2 drastically increased from 323 to 1100 F g −1 after 5000 cycles. Overall, MoS2, NiCo2S4, and NCMS-L showed the Csps of 323, 947, and 1390 F g −1 , respectively. The better capacitive performance of NCMS-L can be ascribed to the strong synergistic contribution of its components, i.e., MoS2 and NiCo2S4. Likewise, the capacitance of NiCo 2 S 4 was increased from 947 to 1121 F g −1 after 5000 cycles. Figure S5a−d represents the electrochemical data for MoS 2 . Similar to NiCo 2 S 4 , the faradaic charge storage ability of MoS 2 is visible from their CV curves and GCD profiles ( Figure S5a,b. However, the cycling stability of MoS 2 drastically increased from 323 to 1100 F g −1 after 5000 cycles. Overall, MoS 2 , NiCo 2 S 4 , and NCMS-L showed the C sp s of 323, 947, and 1390 F g −1 , respectively. The better capacitive performance of NCMS-L can be ascribed to the strong synergistic contribution of its components, i.e., MoS 2 and NiCo 2 S 4 . For NCMS-L, Ni 2+ and Co 3+ are combined with OH − to produce Ni 3+ and Co 4+ during charging. However, K + is inserted into the active material and has a redox reaction on the surface of MoS 2 during discharging [15]. These results explain the increase in C sp of NCMS-L and a considerable increase in the coulombic efficiency from 73% to 123% over 20,000 cycles. On the other hand, it takes a long time for K + ions to penetrate the structure of NCMS-L and have a redox reaction with MoS 2 . After 35,000 cycles, the cycling process was suspended for one week to ensure the complete diffusion of the electrolyte ions into the active material, obtaining enhanced capacitance retention of 192%. To understand the individual contributions of NiCo 2 S 4 and MoS 2 on the cycling stability of NCMS-L, an EIS analysis was performed. After 5000 cycles, the ESR of bare NiCo 2 S 4 increased from 0.53 to 0.6 Ω ( Figure S4c), whereas it decreased from 1.86 to 0.58 Ω for bare MoS 2 ( Figure S5c). The significant decrease in ESR for MoS 2 is well supported by the substantial enhancement of discharge time, as shown in Figure S5d. The morphological analysis of these electrodes after the cycle test reveals a significant change in the structure of MoS 2 from clusters to coral ( Figure S3b). However, no significant change in morphology has been observed for NiCo 2 S 4 ( Figure S3c).
Interestingly, during the pause of the cycling test for two weeks, the morphology of MoS 2 was further changed from coral to chunks ( Figure S7a). However, no significant change in the morphology of NiCo 2 S 4 has been observed after the pause of the cycle test ( Figure S7b). This phenomenon indicates that MoS 2 undergoes drastic structural reformation during the cycling test as well as during the pause of the cycle test. This fact also supports the electrochemical reconstruction of NCMS-L during the cycle test. Therefore, it can be concluded that MoS 2 has majorly contributed to the enhanced electrochemical performance of NCMS-L over long-term cycle life. The enhanced cycling stability of MoS 2 is the driving force of such boosted cycling stability of the composite.
To further estimate the prospective of the NCMS-L electrode for practical applications, an asymmetric supercapacitor device was designed with activated carbon (AC) as the negative electrode, NCMS-L as the positive electrode, and a 3 M KOH aqueous solution as the electrolyte.
The mass of the negative and positive electrodes was adjusted based on the charge balance theory (q + = q − ), as shown in the following equation: Therefore, the mass ratio of the electrode materials was calculated using Equation (12).
where C s , ∆V, and m are the C sp , potential window, and mass of active materials, respectively. The mass ratio of NCMS-L and AC was 0.26, and the total mass of the two electrodes was 6.3 mg. Figure 9a represents the CV curves of the NCMS-L//AC hybrid supercapacitor device within potential limit of 0 to 1.6 V at different scan rates from 5 to 100 mV s −1 . The CV curves indicate the presence of redox peaks, indicating the Faradaic charge storage mechanism. Figure 9b presents the GCD profiles at various current densities of 0.16, 0.32, 0.47, 0.79, 1.27, and 1.59 A g −1 , respectively. The maximum C sp of the device was calculated to be 90 F g −1 at a CD of 0.16 A g −1 . The device also delivered a high-rate capability of 64% after a 10-fold increase in the CD (Figure 9c). As shown in Figure 9d, the device exhibited a long cycle life over 15,000 cycles, which is better than some of the reported devices (Table S1). The device retained 111% of its initial capacitance during the first 1500 cycles. The initial increase in capacitance can be attributed to the steady activation of electrode material. The device exhibited a capacitance retention of 102% after 15,000 cycles. Moreover, it also displayed 98% retention of its initial coulombic efficiency after 15,000 cycles. The enhanced cycling stability of the device can be ascribed to the porous nature of the positive electrode, the synergistic contribution of the individual components of the composite, and the better chemical stability of the carbon black (negative electrode). The device also displayed higher E D than the other related devices, as shown in the Ragone plot ( Figure 9e) [13,[33][34][35]. Based on the equations, E D = 0.5 CV 2 and P D = E D /t, the maximum E D was calculated to be 31.9 W h kg −1 at a P D of 0.13 kW kg −1 , and the highest P D was 1.26 kW kg −1 at the corresponding E D of 20.7 Wh kg −1 . The ESR of the device in the first cycle was approximately reduced to half that of the three-electrode system with a value of 0.22 Ω. However, it was further increased to 0.32 Ω after 15,000 cycles (Figure 9f). The electrode displayed decent capacitance, low ESR, and enhanced cycling stability. Such enhanced electrochemical performance of NCMS-L can be attributed to the following factors: 1. The synergistic contribution of each composite component is highly responsible for such enhanced electrochemical performance. The combination of highly capacitive The electrode displayed decent capacitance, low ESR, and enhanced cycling stability. Such enhanced electrochemical performance of NCMS-L can be attributed to the following factors: 1.
The synergistic contribution of each composite component is highly responsible for such enhanced electrochemical performance. The combination of highly capacitive NiCo 2 S 4 and highly conductive MoS 2 is feasible for fabricating high-performance supercapacitor electrodes.

2.
The enhanced cycling stability of the composite can be attributed to its electrochemical reconstruction during the cycling test.

3.
The porous morphology of the composite (NCMS-L) is favorable for the easy transport of electrolyte ions during the electrochemical test. 4.
The enhanced mechanical strength of MoS 2 restricted the structural deformation of the electrode during the long-term cycling test.

Conclusions
Advanced composite electrodes based on NiCo 2 S 4 and MoS 2 with different morphologies have been synthesized through facile solvothermal processes. Benefiting from a rich faradaic charge storage mechanism, the electrodes displayed a promising electrochemical performance in high capacitance and low ESR. Nevertheless, the composite electrode also exhibited long-term cycle life with negligible capacitance fading. Overall, this composite material can be designated one of the striking candidates for future energy storage devices.